06 Strengthening Mechanisms

Suranaree University of Technology May-Aug 2007

Strengthening mechanismsStrengthening mechanisms

Subjects of interest

Introduction/Objectives

Grain boundary strengthening

Yield-point phenomenon

Strain ageing

Solid-solution strengthening

Strengthening from second phase particles

Martensitic strengthening

Strain hardening or cold working

Bauschinger effect

Preferred orientation (texture)

Chapter 6

Tapany Udomphol

Suranaree University of Technology . May-Aug 2007

ObjectivesObjectives

Different types of strengthening mechanisms in metals

which improve mechanical properties will be highlighted

in this chapter.

This also includes the nature of grain boundaries and

their effects on the strengthening mechanisms, the

influences of solute atoms, second phase particles, and

fibre on the strengthening mechanisms.

Other strengthening mechanisms such as strain

hardening, martensitic hardening and cold working on the

mechanical properties of the materials will also be

discussed.

Tapany Udomphol


IntroductionIntroduction

Strengthening

mechanisms

Martensitic

strengthening

Cold working

Grain boundary

strengtheningFibre

strengthening

Solid-solution

strengthening

Strain ageing

Strain hardening

Fine-particle

strengthening

To obtain

material

strength

The ability of a metal to

plastically deform depends

on the ability of

dislocations to move.

Strengthening

techniques rely on

restricting dislocation

motion to render a

material harder and

stronger.

Sometimes

ductility or

toughness are

sacrificed.


Grain boundary strengtheningGrain boundary strengthening

Grain boundariesGrain boundaries

Grain boundary separates two

grains having different

crystallographic orientations.

Grain boundary structure contains

grain boundary dislocations,

which are not mobile and produce

extensive slip.

Schematic atomic model of

a grain boundaryDislocation model of grain

boundary

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High and low angle grain boundariesHigh and low angle grain boundaries

High - angle grain boundary high surface energy

Low - angle grain boundary low surface energy

High energy grain boundary

serves as preferential sites

for solid state reactions;

1) Diffusion

2) Phase transformation

3) Precipitation

Schematic diagram showing low- and

high-angle grain boundaries.

Angle of misalignment

Angle of misalignment

High-angle

grain

boundary

Low-angle

grain

boundary

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Low angle grain boundariesLow angle grain boundaries

The angular difference in

orientation between the grain is .Diagram of low-angle grain boundary

Along the boundary the atoms adjust

their position by localised deformation

to produce a smooth transition from

one grain to the other.

Where the atom planes end on the

grain boundaries, it is therefore

considered to have an array of

dislocations.

Tapany Udomphol


SubgrainSubgrain boundariesboundaries

Subgrain boundary network in

Fe-3% alloy.

Subgrain boundaries are low-angle

boundaries, with lower-energy

boundaries than the grain

boundaries. therefore etch less

readily than grain boundaries.

If the angle is small the distance between dislocation is large. It is

often possible to observe pits

(corresponding to sites for edge

dislocations) along the boundaries,

see fig.

250 x 1000 x

Etch-pit structures along low-angle

grain boundaries in Fe-Si alloy.

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PolygonizationPolygonization

Polygonization occurs when a single crystal is bent to

a relatively small curvature and then annealed.

Bending results in an excess number of dislocations of similar

sign distributing along the bend-glide plane.

After heating, dislocations group themselves into the lower-

energy configuration of a low-angle boundary, forming a

polygonlike network.

Movement of dislocations to produce polygonization.

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Deformation of grain boundaries.Deformation of grain boundaries.

Ashbys model of deformation

of a polycrystal.

Discontinuity due to grain boundaries

leads to more complex deformation

mode in polycrystals than in single crystals.

Individual grain is constrained since

mechanical integrity and coherency are

maintained along the grain boundaries,

causing different deformation between

neighbouring grains.

A polycrystal macroscopically deforms

as the stress is applied. Slips operate in

each grains which produces overlaps

and voids at boundaries, fig (a),(b).

These overlaps and voids can be

corrected by introducing geometrically

necessary dislocations at (c),(d).

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Plastic deformation of polycrystalline Plastic deformation of polycrystalline

metalsmetals

Note: More slip systems are usually

operate near the grain boundary, the

material is usually harder near the

boundary than the grain interior.

Slip lines on the surface of a

deformed polycrystalline copper

Due to random crystallographic

orientations of the numerous grains, the

direction of slip varies from one gain to

another.

Fig. shows two slip systems operate in

each grain and variation in grain orientation

is indicated by the different alignment of

slip lines.

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Grain boundary slidingGrain boundary sliding

At T > 0.5Tm, deformation can occur by sliding along

the grain boundaries.

Temperature

Strain rateTendency for grain boundary

sliding (as in creep).

EquicohesiveEquicohesive temperaturetemperature

Above the equicohesive

temperature, the grain boundary

region is weaker than the grain

interior.

Strength increases with

increasing grain size.

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Strengthening from grain boundariesStrengthening from grain boundaries

There are two important roles of the grain boundary which acts as

a barrier to dislocation motion;

1) Difficulty for a dislocation to

pass through two different

grain orientations (need to

change direction).

2) The atomic disorder within a

grain boundary region

contributes to a discontinuity

of slip planes from one grain

to another.

The motion of a dislocation as it encounters

a grain boundary.

Grain A Grain B

Slip plane

Grain boundary

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HallHall--PetchPetch relationrelation

A fine-grained material is harder and stronger than one that is coarse

grained since greater amounts of grain boundaries in the fine-grained

material impede dislocation motion.

The general relationship between the yield stress (tensile strength)

and grain size was proposed by Hall and Petch.

21+= kDio Eq. 1

Where o = the yield stressi = the friction stress or resistance to

dislocation movement

k = the locking parameter or hardening

contribution from grain boundary.

D = grain diameter

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Hall Hall -- PetchPetch relation and relation and

dislocation piledislocation pile--up modelup model

D

The dislocation model for the Hall-

Petch equation was originally based on

the idea that grain boundaries act as

barriers to dislocation motion.

Dislocations will be sent out from the

source at the centre of a grain of D

diameter to pile up at grain boundary.

The number of dislocations at the

pile-up is

Gb

Dkn s

4

=

Eq. 2

Where s is the average resolved shear stress

k is a factor close to unity

The stress at the tip of the pile-

up must exceed some critical

shear stress c to continue slip past the grain-boundary barrier

21

21

2

4

,4

+=

+=

===

kD

D

Gb

Gb

Dn

i

c

i

is

s

sc

Then

Eq. 3

Note: for large pile-upsTapany Udomphol


Grain size determinationGrain size determination

Since the size of the grain is usually associated with mechanical

properties of the materials, determination of the grain size is

therefore of importance.

The obtained parameters can

be specified in terms of;

1) Average grain volume

2) Average grain diameter

3) Average area

4) Maximum diameter

5) Minimum diameter

6) Aspect ratio

There are a number of

techniques utilised for grain size

measurement;

1) Intercept method

2) ASTM standard comparison

charts (grain number)

3) Image analyser

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Intercept methodIntercept method

Intercept method is carried out by measuring the mean number

of intercepts of random test lines with grain boundaries per unit

length of test line NL.

Strength lines of the same length L

are drawn though several

photomicrograph with a known scale.

The grain intersected NL by each line

segment are counted.

The average grain diameter is

obtained by 200 x

MN

LD

L

=Where M is a linear

magnification of the

photomicrograph.

Note: The grain size obtained by this

method will be somewhat smaller

than the actual grain size. In some

case, a factor 2/3 is used.Eq. 4

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ASTM standard comparison chartASTM standard comparison chart

Comparison of the grains at a fixed magnification with the

American Society for Testing and Materials (ASTM)

grain size charts.

The ASTM grain-size number G

is related to na, the number of

grains per mm2 at a

magnification of 1 x by the

relationship

anG ln4427.19542.2 +=

Eq. 5

Tapany Udomphol


Example: If a steel has a value of i = 150 MPa and k = 0.70 MPa.m1/2, what is the value of the yield stress if the grain size is ASTM no.6.

From Eq.6

262 104964964427.1

9524.26exp

4427.1/)9542.2(ln

==

+=

+=

mmmn

Gn

a

a

Grain diameter

MPakD

mD

mDmD

nDornD

io

aa

3.254)149)(70.0(150

1491

107.44,1020

/1/1

21

21

62102

2

=+=+=

=

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Yield point phenomenonYield point phenomenon

Metals, particularly low-carbon steel, show a localised heterogeneous

transition from elastic to plastic deformation. Yield point elongation.

Yield point behaviour in BCC metals

The load after the upper yield point suddenly

drop to approximately constant value (lower

yield point) and then rises with further strain.

The elongation which occurs at constant load

is called the yield-point elongation, which are

heterogeneous deformation.

Lder bands or stretcher strains are formed at

approximately 45o to the tensile axis during yield

point elongation and propagate over the

specimen.

Note: The yield point phenomenon has also been observed

in other metals such as Fe, Ti, Mo, Cd, Zn, Al alloys.Tapany Udomphol


The upper yield pointThe upper yield point

The upper yield point is associated with small amounts of

interstitial or substitutional impurities.

The solute atoms (C or N) in low carbon steel, lock the

dislocations, raise the initial yield stress.

The breakaway stress required to pull a dislocation line away

from a line of solute atoms is

22

orb

A Eq. 6

Where A is 4Gba3 , a is atomic radiusro is the distance from the

dislocation core to the line of

solute atoms ~ 0.2 nm.

When the dislocation is pulled

free from the solute atoms, slip

can occur at lower stress. the

lower yield point.

The magnitude of the yield-point

effect depends on interaction

energy, concentration of solute

atoms.

Note: Upper yield point is promoted by using elastically rigid machine,

careful axial alignment of specimen (free from stress concentrations,

high strain rate, low temperature.)Tapany Udomphol


Strain ageingStrain ageing

Strain ageing is a phenomenon in which the metal increase

in strength while losing ductility after being heated at

relatively low temperature or cold-working.

Strain ageing in low-

carbon steel.

The reappearing of the

(higher) yield point after

ageing is obtained, see fig.

Reloading at X and straining to Y does not

produce yield point.

After this point if the specimen is reloading

after ageing (RT or ageing temp) the yield

point will reappear at a higher value.

This reappearance of the yield point is due

to the diffusion of C and N atoms to

anchor the dislocations.

N has more strain ageing effect in iron than

C due to a higher solubility and diffusion

coefficient.

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Stretcher strainsStretcher strains

Strain ageing should be eliminated in deep drawing steel since it

leads to surface marking or stretcher strains.

To solve the problem, the amount of C and N should be lowered by

adding elements such as Al, V, Ti, B to form carbides or nitrides.

Stretcher strain in low-carbon steel

Relation of stretcher strain in

stress-strain curve

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Serrated stress strain curvesSerrated stress strain curves

Strain ageing increases yield point but lower ductility.

Strain ageing is also associated with serrated stress-strain

curves or repeated yielding, due to high speed of diffusion of

solute atoms to catch and lock dislocations.

This dynamic strain ageing is also called

Portevin-LeChatelier effect.

Portevin-LeChaterier effect.

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Blue brittlenessBlue brittleness

Blue brittleness occurs in plain carbon steel in which discontinuous

yielding appears in the temperature range 500 to 650 K.

During this blue brittleness region, steels show

Decreased tensile ductility.

Decreased notched-impact resistance.

Minimum strain rate sensitivity.

Note: This is just an accelerated strain aging by temperature.

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SolidSolid--solution strengtheningsolution strengthening

There are two types of

solid solutions;

2) Interstitial solid solution: The

solute atoms are of smaller size

than the solvent atom, rendering

the solute atoms to occupy the

interstitial sites in the solvent lattice.

Note: solid solution is compositionally homogeneous, the solute (impurity)

atoms are randomly distributed throughout the matrix.

1) Substitutional solid solution:

the solute and solvent atoms are

similar in size, rendering the

solute atoms to occupy lattice

point of the solvent atoms.

Solute atoms are introduced into

the matrix (solvent atoms).

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Factors affecting solubility of solute atomsFactors affecting solubility of solute atoms

The solubility of the solute atoms in the host matrix (solvent)

can be determined by several factors;

1) Atomic size factors : Solid solution is appreciable when

the difference in atomic radii between the tow atoms is <

~15%, otherwise creating substantial lattice distortion.

2) Crystal structure : Similar crystal structure of metals of

both atom types types are preferred.

3) Electronegativity : The more electropositive one element

and the more electronegative the other, the more tendency

to form an intermetallic compound than solid solution.

4) Valences : A metal will have more of a tendency to dissolve

another metal of higher valency than one of a lower

valency.

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Effects of solute alloy additions on Effects of solute alloy additions on

stressstress--stain curvestain curve

The addition of solute atoms raises the

yield stress and the stress-stain curve

as a whole.

Therefore from Eq.1

21+= kDio

The solute atoms should have more

influence on the frictional resistance to

dislocation motion i than the locking of dislocation k.

Solute atoms Strengthening effect

Effects of solute atoms on

stress-strain curves.

Pure polycrystal

C1% solute

Alloys

C2>C1 %solute

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Effects of solute alloy additions on tensile Effects of solute alloy additions on tensile

propertiesproperties

Impurity atoms

Tensile strength

Yield stress

Ductility

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Lattice strain due to solute atomsLattice strain due to solute atoms

Lattice strains produced by the introduction of solute atoms

can be divided into:

1) Tensile lattice strain

Smaller solute atoms are

introduced, imposing

tensile lattice strain to the

host atoms.

2) Compressive lattice strain

Larger solute atoms are

introduced, imposing

compressive lattice strain to

the host atoms.

Tapany Udomphol


Interactions between solute atoms Interactions between solute atoms

and dislocationsand dislocations

Solute atoms can interact with dislocations by

the following mechanisms:

1) Elastic interaction

2) Modulus interaction

3) Stacking-fault interaction

4) Electrical interaction

5) Short-range order interaction

6) Long-range order interaction

Note: 1, 2, 6 are insensitive to temperature and

influence at about 0.6Tm.

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Elastic interaction Strengthening due to elastic interaction is proportional to the

misfit between solute atoms and dislocations giving elastic

field around surrounding them.

Modulus interaction The presence of the solute atom locally alter the modulus of

the crystal. Solute atom with small shear modulus will reduce

the energy of the strain field.

Solute atoms

within the

stacking fault

Stacking-fault interaction

Stacking fault

energy

Separation

between partial

dislocations

Tapany Udomphol


Electrical interaction The solute atoms having charge can interact with dislocation

which have electrical dipoles. weak.

Short-range order interaction Strengthening by short-range order interaction is due to more

work which has to put in when dislocations try to move pass

through the short range ordered atoms.

Long-range order interaction Alloys having a long-range periodic arrangement of dissimilar

atoms develop superlattice. The stress required to move a

dislocation through a long-range region is high and the rate of

strain hardening is higher in the ordered condition than the

disordered state.

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Strengthening from second phaseStrengthening from second phase

Many commercial alloys are composed of two or more

metallurgical phases which provide strengthening effects:

Two phase aggregates

Second phase/intermetallic particles

Precipitation hardening

Fibering structure

1)These are heterogeneous on a microscopic scale or maybe

homogeneous on a macroscopic scale.

2) Strengthening from second phases is normally additive to the

solid solution strengthening produced in the matrix.

Note:

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Strengthening by twoStrengthening by two--phase aggregatesphase aggregates

Two-phase aggregates

The size of the second phase particles

are of similar size to that of the matrix.

Examples ;

Beta brass particles in an alpha

brass matrix

Pearlite colonies in the ferrite

matrix in annealed steels

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Strengthening by second phase particlesStrengthening by second phase particles

Dispersed second-phase

particles in the matrix.

The second phase or intermetallic

particles are much finer (down to

submicroscopic dimensions) than the

grain size of the matrix.

The second phase particles produce

localised internal stresses which

alter the plastic properties of the

matrix.

Examples ;

Second

phase

particles in

matrix.

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Factors influencing secondFactors influencing second--phase particle phase particle

strengtheningstrengthening

Particle size

Particle shape

Number (Vf)

Distribution

(interparticle spacing)

Strength

Ductility

Strain hardening

Note: Its almost

impossible to vary these

factors independently in

experiments.

If the contributions of each phase are independent, the properties

of the multiple phase alloy is the summation of a weighted average

of individual phases.

nnavg VVV ...2211 ++= Eq. 7

Eq. 8nnavg VVV ...2211 ++=

For example;

Stress

Strain

Where the volume

fraction V

V1 + V2 ++ Vn = 1

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Estimate flow stress of twoEstimate flow stress of two--phase alloyphase alloy

The average property in the two-phase alloy will increase with

the volume fraction Vf of the strong phase.

It is more often that the second phase is stronger than the

matrix but not all second-phase particles produce strengthening

effects.

The strong bonding between particles and matrix is required to

be able to produce strengthening effects.

0.0 f2

0.5 f2

1.0 f2

1

2

At equal strain

0.0 f2

0.5 f2

1.0 f2At equal stress

21

(a) At equal strain (b) At equal stress

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Deformation in two Deformation in two

ductile phase alloysductile phase alloysDeformation in alloy Deformation in alloy

of a ductile and of a ductile and

brittle phasebrittle phase

Depending on the Vf of

the two phases and the

total deformation.

Slip will occur first in the

weaker phase

Not all second phase

particles produce

strengthening effects.

Mechanical properties depends

on how the hard brittle phase

distribute throughout the softer

matrix.

Homogeneously distributed hard

particles promote strength.

Continuously distributed along

the grain boundaries leads to

brittle fracture. reduce

strength.

Tapany Udomphol


Microstructure dependence of yield stress Microstructure dependence of yield stress

in steelsin steels

Mean free path, m

S

t

r

e

s

s

a

t

0

.

2

s

t

r

a

i

n

Flow stress vs. log of mean

free ferrite path in steels.

Gensamer et al studied the

influence of different microstructures

obtained from annealed,

normalised and spheroidized

steels (aggregates of cementites

and ferrite).

The 0.2% was inversely proportional to the logarithm of mean free ferrite

path (interparticle spacing).

Interparticle

spacing

Yield stress

Tapany Udomphol


Precipitation hardeningPrecipitation hardening

Precipitation hardening or age

hardening requires the second phase

which is soluble at high temperature

but has a limited solubility at lower

temperatures.

Solution treating at

high temperature,

then quenchingSecond phase is in solid solution.

Ageing at

low temperature

Precipitation of the second phase,

giving strengthening effect.

Note: In precipitate-hardened system, there is coherency between the

second-phase particle and the matrix.

But in dispersion-hardened system, there is no coherency.

Example: Age hardening aluminium alloys

Copper-beryllium alloys

Al-Cu phase

diagram

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The formation of coherency precipitateThe formation of coherency precipitate

Variation of yield stress with

ageing time.

A number of steps occurs during precipitation hardening.

After quenching from solid solution the

alloy contains areas of solute

segregation or clustering. GP zone.

This clustering is GP[1] produces local

strain giving higher hardness than the

matrix.

The hardness of the GP zone increases

with ageing time, developing GP[2] or .

Precipitate is coherent with the matrix. further increase in hardness.

Further ageing produces , (not coherentwith the matrix). lowering the hardness.

Tapany Udomphol


Deformation of alloys with fine particle Deformation of alloys with fine particle

strengtheningstrengthening

Case study in deformation of Al-4.5%Cu single crystal

S

h

e

a

r

s

t

r

e

s

s

Shear strain

Pure aluminium

Solid solution

After solution treated and quenched,

copper is in supersaturated solid

solution, giving higher yield stress

than pure aluminium.

The yield stress increases when the

crystal is aged to form coherent GP zone.

Yield drop and low strain hardening

suggest that dislocations cut through the

zone once the stress reaches a high

enough value.

Aged to form

GP zone

Aged to peak

hardness

Strain hardening significantly

increase when the crystal is aged to

peak hardness. Dislocations are

short and move around particles.

Over-aged condition produces

coarse noncoherent particles, giving

low yield stress, high strain

hardening.

Over aged

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Factors affecting precipitation hardeningFactors affecting precipitation hardening

Particle size, shape, volume

fraction and distribution are

key factors in improving

precipitation hardening (cannot

vary independently).

High strength alloys seem to

consist of fine strong particles

well distributed in deformed

matrix.

Fine hard particles increase strength

by cutting dislocations dislocation

tangles increasing strain hardening.

Deformed matrix bares the load

which makes fracture more

difficult.

Example: For a given Vf

Particle size Interparticle

spacing

Interparticle spacing

Interparticle spacing

f

f

V

rV

3

)1(4 =

Where Vf is the volume fraction of

spherical particles of radius r.

Eq. 9

Tapany Udomphol


Properties affecting strengthening Properties affecting strengthening

mechanisms by particlesmechanisms by particles

Ordered structure

introduce anti-phase boundaries.

good high temperature strength.

Coherency strain

Misfit between particles and matrix

produces strain field improving

strength.

Stacking-fault energy

Yield stress increases with the

difference in stacking fault energy

between the particle and the matrix.

Modulus effect

Modulus difference between the

matrix and the particles produces

strength but it is not the case in most

alloys.

Interfacial energy and

morphology

High particle-matrix surface energy

leads to higher strength. (rely on

surface-to-volume ratio or morphology)

Lattice friction stress

Peierls stress in particle and matrix

produce strengthening effect.

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Interaction between fine particles and Interaction between fine particles and

dislocationsdislocations

1) Particles maybe cut by

dislocation

Second phase particles act in two distinct ways to retard the

motion of dislocations.

2) Particles allow dislocation to

bypass/bow around them.

When the particles

are small / soft.

In over aged noncoherent precipitates.

Bowing of dislocations around particles

leaving dislocation loops behind.

Orawans

mechanism

of

dispersion

hardening.

Stress required to force

dislocation between particles;

Gbo = Eq. 10

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Role of slip characterRole of slip character

The slip character can be

characterised in to;

Planar or wavy

Coarse or fine

Fine wavy slip homogeneous

deformation, giving best ductility at a

given strength level. Particles which are

by passed by dislocations lead to fine

wavy slip.

Coarse planar slip promotes

brittle failure. Particles which is easily

sheared by dislocations tend to

produce coarse planar slips.

Planar slips in aged

hardenable Al alloy.

Coplanar bands in

warm rolled nitrogen-

alloyed austenistic

stainless steel

Wavy slips

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Fibre strengtheningFibre strengthening

Ductile metals can be reinforced using relatively stronger fibres.

Very high strength whiskers of Al2O3, or SiC fibres have been used

for this purpose.

Fibre-reinforced materials (metal or polymer as matrix) are also

known as composite materials.

High modulus fibres in Fibre-reinforced metals

carry more load than dispersion-reinforced metals.

Fibre-reinforced materials are highly anisotropic.

The matrix transmits the load to the fibres.

protect fibres from surface damage.

separate individual fibres and blunt crack

from fibre breakage.

Note: Variation of stress between

fibres and matrix is complex.Tapany Udomphol

Strength and Strength and modulimoduli of compositesof composites

The rule of mixtures is used to approximate the modulus and

strength of a fibre-reinforced composite.

If a tensile force P is applied

in the direction of the fibre,

and assuming that the strain

of fibre and matrix are similar,

ef = em = ec.

mmff AAP += Eq. 11

Where Af and Am are the cross-

sectional areas of fibre and matrix.

The average composite strength c is


mmffc

c

mm

c

ff

c

c

VV

A

A

A

A

A

P

+=

+==

1=+

+=

mf

mfc

VV

AAAwhere

Eq. 12

Likewise

mmffc VEVEE += Eq. 13

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Example: Boron fibre, Ef = 380 GPa, are made into

a unidirectional composite with an aluminium matrix,

Em = 60 GPa. What is the modulus parallel to the

fibres for 10 and 60 volume%.

GPaEV

GPaEV

EVVEE

cf

cf

mfffc

252)60(4.0)60.0(380,60.0

92)60(9.0)10.0(380,10.0

)1(

=+==

=+==

=

Tapany Udomphol

StressStress--strain curves of the fibre, matrix and strain curves of the fibre, matrix and

fibrefibre--reinforced compositereinforced composite

Stage 2 : Matrix deforms plastically

but fibres deform elastically.

Strain

S

t

r

e

s

s

Fibre

Composite

Matrix

Stage I

Stage 2

Stage 3

Stage 1 : Both fibres and

matrix undergo elastic

deformation.

Stage 3 : Both matrix and fibres

undergo plastic deformation.

The load is transferred

from ductile matrix to

strong fibres.

Breakage or pull-out of

fibres increase the

strength.

Suranaree University of Technology May-Aug 2007Tapany Udomphol


Theoretical variation of Theoretical variation of

composite strength with composite strength with

volume fraction of fibresvolume fraction of fibres

The minimum volume fraction

of fibre which must be exceeded to

have real reinforcement.

'

'

)(mfu

mmu

critfV

=

Eq. 14

The critical fibre volume which

must be exceeded for fibre

strengthening to occur.

'

'

(min)mmufu

mmu

fV +

=

Eq. 15C

o

m

p

o

s

i

t

e

s

t

r

e

n

g

t

h

Volume fraction of fibres0 1.0

V f (min)

V f (crit)

f

u

m

u is the ultimate tensile strength of the composite

f is the strength of the fibrem is the flow stress in the matrix

Strain

Stress

Fibre

Composite

Matrix

f

c

m

mc, , , , f

m

Martensite strengthening

Martensitic strengthening is obtained when austenite is

transformed into martensite by a diffusionless shear-type

process in quenching.

Martensitic transformation occurs in

many alloy systems but steels has

shown the most pronounced effect.

Hardness in various products in

steel.

High strength of martensite is due

to two main contributions;

Slip barriers from (1) conventional plate

martensite structure with a unique habit plane

and an internal parallel twins of each 0.1 mm

thick within the plate and (2) Block martensite

structure containing a high dislocation density of

109 to 1010 mm-2.

Carbon contents (


AusformingAusforming processprocess

Ausforming is a thermo-mechanical process where steel is

plastically deformed (>50%) usually rolling and then quenched to

below the Ms to form martensite.

T

e

m

p

e

r

a

t

u

r

e

TTT diagram showing steps

in ausforming process.

Plastic deformation of austenite should

be done without transformation to

pearlite or bainite.

Highest strengths are achieved by the

greatest possible deformation at the

lowest temperature at transformation

does not occur.

Uniformly distributed dislocations of high density (1011 mm-2) and

precipitation provides sites for dislocation multiplication and

pinning, contribute to very high strength (2-3 GPa) with 40-20% RA.

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Strain hardening or cold workingStrain hardening or cold working

Cold-work structure occurs when plastic deformation carried out

at in a temperature region and over a time interval such that the

strain hardening is not relieved.

Cold worked structure contains

dislocation ~ 1011 mm-2, while

annealed structure possesses

~104 to 106 mm-2.

(a) Deformed to 10% (b) Deformed to 50%

Dislocations in cell walls.

As the deformation proceeds, the high

density dislocations tangles form the

cell walls.

About 10% of energy input in cold work

process is stored in the lattice.

Stored energyTemp Strain rate

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Strain hardeningStrain hardening

Strain hardening or cold working is used to harden alloys that

do not respond to heat treatment.

Variation of tensile properties with

amount of cold-work.

Cold work Strength

Ductility

The rate of strain hardening is lower

in HCP than in cubic metals.

The final strength of cold-worked

solid solution alloy is almost always

greater than that of the pure metal

cold-worked to the same extent.

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Annealing of coldAnnealing of cold--worked metalworked metal

Annealing of the cold worked structure at high temperature

softens the metal and reverts to a strain-free condition.

Annealing restores the ductility to a metal that has been

severely strain hardened.

Annealing can be divided into three distinct processes;

1) Recovery

2) Recrystallisation

3) Grain growth

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Recovery, Recovery, recrystallisationrecrystallisation, grain growth, grain growth

Recovery : the restoration of the

physical properties of the cold-

worked metal without any

observable change in microstructure.

Strength is not affected.

Recrystallisation : the cold-

worked structure is replaced by a

new set of strain-free grains.

Hardness and strength decrease

but ductility increases.

Grain growth : occurs at higher

temperature where some of the

recrystallised fine grains start to

grow rapidly. Grain growth is

inhibited by second phase particles

to pin the grain boundaries.

Properties change during recovery,

recrystallisation and grain growth


Variables affecting Variables affecting recrystallisationrecrystallisation

behaviourbehaviour

1) The amount of prior deformation

2) Temperature

3) Time

4) Initial grain size

5) Composition

6) Amount of recovery prior to start

the recrystallisation.

There are six variables affecting

recrystallisation behaviour.Degree of deformation Trecrys

Degree of deformation

Tanneal , GSrecrys

Impurity decrease

recrystallisation temperature.

Solid solution alloying additions

raise the recrystallisation

temperature.

GSoriginal Cold work

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Preferred orientation (texture)Preferred orientation (texture)

Severe deformation produces a reorientation of the grains into

a preferred orientation. Certain crystallographic planes tend to

orient themselves in a preferred manner with respect to the

maximum strain direction.

Note: the deformation texture cannot in general be eliminated by

an annealing operations

The preferred orientation resulting from plastic deformation is

strongly dependent on the available slip and twining systems,

but not affected by processing variable such as die angle, roll

diameter, roll speed, etc.

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Grain orientation by EBSD analysisGrain orientation by EBSD analysis

EBSD analysis employs back scattered

electrons to give grain orientation

information.

Homogeneously distributed.

Preferred orientation.

SEM micrograph Orientation map Pole figure Inverse pole figure

Normal to processing

direction

[111]

[101][001]

50 m

50 m

Extruded bar

Rolled plate

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Mechanical Mechanical fiberingfibering (fibrous texture)(fibrous texture)

Fibrous texture is produced along the maximum stress direction

acting on the materials.

Inclusions, cavities and second phase constituents are aligned in

the main direction of mechanical working.

Alignment of carbides along the

extrusion direction in -Ti alloy.

Mechanical fibering increases

mechanical properties along the

working (fibre) direction, with the

transverse direction having inferior

properties. anisotropic properties.

Carbides

The geometry of the flow and the

amount of the deformation are the most

important variables.

Extrusion direction

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ReferencesReferences

Dieter, G.E., Mechanical metallurgy, 1988, SI metric edition,

McGraw-Hill, ISBN 0-07-100406-8.

Sanford, R.J., Principles of fracture mechanics, 2003, Prentice

Hall, ISBN 0-13-192992-1.

W.D. Callister, Fundamental of materials science and

engineering/ an interactive e. text., 2001, John Willey & Sons, Inc.,

New York, ISBN 0-471-39551-x.

Hull, D., Bacon, D.J., Introduction to dislocations, 2001, Forth

edition, Butterworth-Heinemann, ISBN 0-7506-4681-0.

Smallman, R.E., Bishop, R.J., Modern physical metallurgy &

materials engineering, 1999, sixth edition, Butterworth-Heinemann,

ISBN 0-7506-4564-4.

www.composite-bydesign.com

www.mdi.espci.fr

www.mtm.kuleuven.ac.be

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ReferencesReferences

Aladar A. Csontos and Edgar A. Starke, The effect of inhomogeneous

plastic deformation on the ductility and fracture behavior of age

hardenable aluminum alloys, International Journal of Plasticity, Vol. 21,

Issue 6, June 2005, p. 1097-1118.

S. Frchard, A. Redjamia, E. Lach and A. Lichtenberger, Mechanical

behaviour of nitrogen-alloyed austenitic stainless steel hardened by

warm rolling, Materials Science and Engineering: A, Vol. 415, Issues 1-2,

2006, p. 219-224.

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Documents

06 Strengthening Mechanisms